CN109504881A - A kind of Al-Si-Cu-Mg-Ni-Sr alloy material and preparation method thereof and piston - Google Patents
A kind of Al-Si-Cu-Mg-Ni-Sr alloy material and preparation method thereof and piston Download PDFInfo
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- CN109504881A CN109504881A CN201811529576.1A CN201811529576A CN109504881A CN 109504881 A CN109504881 A CN 109504881A CN 201811529576 A CN201811529576 A CN 201811529576A CN 109504881 A CN109504881 A CN 109504881A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
- C22C21/04—Modified aluminium-silicon alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
- F02F—CYLINDERS, PISTONS OR CASINGS, FOR COMBUSTION ENGINES; ARRANGEMENTS OF SEALINGS IN COMBUSTION ENGINES
- F02F3/00—Pistons
- F02F3/0084—Pistons the pistons being constructed from specific materials
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
- F02F—CYLINDERS, PISTONS OR CASINGS, FOR COMBUSTION ENGINES; ARRANGEMENTS OF SEALINGS IN COMBUSTION ENGINES
- F02F2200/00—Manufacturing
- F02F2200/06—Casting
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- Pistons, Piston Rings, And Cylinders (AREA)
Abstract
The present invention relates to technical field of alloy, refer specifically to a kind of Al-Si-Cu-Mg-Ni-Sr alloy material and preparation method thereof and piston, the alloy material by mass percentage containing 12.35% to 13.65% Si, 4.28% to 4.73% Cu, 0.95% to 1.05% Mg, 1.90% to 2.10% Ni, 0.04% to 0.06% Sr, surplus is aluminium and impurity, total impurities≤0.1%.This method passes through targeted design of alloy and uses reasonable melting and Sr Metamorphism treatment technique, in conjunction with heat treating regime appropriate, it can obtain the piston alloy for all having compared with high-tensile in high temperature (300 DEG C) and under room temperature, and since solid solution and aging time are shorter in heat treatment process, comprehensive lower production costs.
Description
Technical field
The present invention relates to technical field of alloy, a kind of Al-Si-Cu-Mg-Ni-Sr alloy material and its preparation side are referred specifically to
Method and the piston made of this alloy material.
Background technique
It is one of important as engine, it is known as the piston of the title of engine " heart ", is mainly used to transmit energy.Engine
High temperature is placed in when work, at the top of part piston, in high-pressure gas, for surface maximum temperature up to 300 DEG C or more, thermic load is big；Its
Skirt section is contacted with cylinder wall, the high variable motion state for being 6m/s to 15m/s in average speed, and lack of lubrication；According to not
Same type, the maximum pressure born are 3MPa to 15MPa.From the point of view of pistons work condition, to guarantee that engine operation is good
It is good, it manufactures alloy used in piston and needs to have that density is small, thermal expansion coefficient is small, heat-conductive characteristic is good, antifriction and wearability
Energy is got well and the performance characteristics such as mechanical performance and processing performance are excellent.And eutectic Al-Si alloy is because in casting character, thermostabilization
Property, wearability and thermal expansivity etc. have some superiority, be commonly applied to manufacture piston details.
Modern automobile industry proposes increasingly higher demands to the alloy material of piston of automobile engine, especially applies
In the extraordinary piston of high-end automobile engine, the alloy material requirement of this piston is manufactured in high temperature (300 DEG C) and room temperature environment
Under all meet the requirement of higher tensile strength.However not yet discovery can improve two kinds of temperature conditions after individually adding simultaneously at present
The intensified element of the mechanical property of lower eutectic Al-Si alloy, therefore, it is necessary to by adding a variety of intensified elements and optimizing element
Proportion, then be aided with heat treatment appropriate, develop a kind of multicomponent alloy suitable for making extraordinary piston, it is made to meet one
While fixed hot environment service performance, it is also equipped with superior room temperature environment service performance.
Summary of the invention
The first object of the present invention is to provide one kind and all meets higher tensile strength requirement under high temperature and room temperature environment
Al-Si-Cu-Mg-Ni-Sr alloy material.
The second object of the present invention is to provide a kind of piston made of above-mentioned Al-Si-Cu-Mg-Ni-Sr alloy material.
The third object of the present invention is to provide a kind of preparation method of above-mentioned Al-Si-Cu-Mg-Ni-Sr alloy material.
To realize that above-mentioned first purpose, the present invention provide a kind of Al-Si-Cu-Mg-Ni-Sr alloy material, the alloy material
By mass percentage containing 12.35% to 13.65% Si, 4.28% to 4.73% Cu, 0.95% to 1.05% Mg,
1.90% to 2.10% Ni, 0.04% to 0.06% Sr, surplus be aluminium and inevitable impurity, total impurities≤
0.1%.
In above-mentioned alloy material, alloy element of the Cu as eutectic Al-Si-Cu-Mg-Ni-Sr alloy material can be played
Solution strengthening and refined crystalline strengthening effect, to significantly improve mechanical property of the alloy under heat treatment state.Mg is both Al-Si-Cu-
Solution strengthening phase Mg in Mg-Ni-Sr alloy material2Thermal stability is higher in the constitution element and alloy of Si
Al5Si6Cu2Mg8The constitution element of phase, therefore appropriate addition Mg is remarkably improved the tensile strength and surrender of alloy after heat treatment
Intensity, and refining effect is played to the Si phase in alloy.In addition the high temperature of Al-Si-Cu-Mg-Ni-Sr alloy material can be improved in Ni
Intensity.
Sr is rotten to be mainly shown as the effect of Al-Si-Cu-Mg-Ni-Sr alloy material: alloy is in process of setting, trip
From Sr atomic adsorption constantly block its original twin step in Si phase growth front, while facilitating a large amount of new re-entrant angles again
Twin generates, its growth characteristics is made to be changed into isotropism by original anisotropy.So Eutectic Silicon in Al-Si Cast Alloys is converted by en plaque
Coralliform fiber fines form, and make the end eutectic Si that roundingization transformation occur, so that the room-temperature mechanical property of alloy be made to obtain
To improvement.
To realize that above-mentioned second purpose, the present invention provide a kind of piston, be characterized in that, the piston is by aforementioned Al-
Si-Cu-Mg-Ni-Sr alloy material is made.
To realize that above-mentioned third purpose, the present invention provide a kind of preparation of above-mentioned Al-Si-Cu-Mg-Ni-Sr alloy material
Method, this method include the following steps:
A, ingredient: according to each element mass percent in Al-Si-Cu-Mg-Ni-Sr alloy material be Si:12.35% extremely
13.65%, Cu:4.28% to 4.73%, Mg:0.95% to 1.05%, Ni:1.90% to 2.10%, Sr:0.04% extremely
0.06% and balance aluminum ratio, weigh Al-Si intermediate alloy, Al-Cu intermediate alloy, pure magnesium, Al-Ni intermediate alloy,
Al-Sr intermediate alloy and commercial-purity aluminium；
B, melting: B1, using the weighed commercial-purity aluminium of step A and Al-Si intermediate alloy as in base-material investment smelting furnace plus
Heat is to 770 DEG C to 790 DEG C and keeps constant temperature, and coverture is sprinkled when base-material softening stays, and base-material keeps the temperature after being completely melt and stands,
Then Al-Cu intermediate alloy and Al-Ni intermediate alloy is added, is sufficiently stirred and skims after being completely melt；B2, step B1 is obtained
Melt be cooled to 715 DEG C to 725 DEG C and the pure magnesium that wrap up with aluminium foil be added, then sprinkle coverture and stirring be to industry
Pure magnesium is completely melt, is then skimmed；B3, the obtained solution of step B2 is warming up to 770 DEG C to 790 DEG C and sprinkles covering
Agent is vented deslagging then to refining agent is added in melt, and heat preservation is skimmed after standing；It is added in B4, the melt obtained to step B3
With the Al-Sr intermediate alloy of aluminium foil package and coverture is sprinkled, heat preservation is stood simultaneously after stirring is completely melt to Al-Sr intermediate alloy
It skims；
C, cast: the melt that injection step B is obtained into casting mould obtains alloy cast ingot after cooling；
D, solution treatment: the obtained alloy cast ingot of step C is heated to 510 DEG C, quenches and is cooled to room temperature after keeping the temperature 6h；
E, ageing treatment: the obtained alloy cast ingot of step D is heated to 185 DEG C, is slowly cooled to room temperature, obtains after keeping the temperature 6h
To Al-Si-Cu-Mg-Ni-Sr alloy material.
By above scheme as it can be seen that the room temperature intensity of alloy, above-mentioned Al-Si-Cu-Mg- can be improved in reasonable heat treatment process
Ni-Sr alloy is suitble to be heat-treated by the way of solution treatment+artificial aging (T6), and is determined by experiment best
Heat treating regime is that 510 DEG C × 6h is dissolved (quenching)+185 DEG C × 6h timeliness.
Heat treatment is mainly shown as the effect of Al-Si-Cu-Mg-Ni-Sr alloy: eliminating alloy internal segregation, raising group
Uniformity is knitted, and improves the stability of tissue, while eliminating internal stress, and improve machining property；Because alloying element is in α phase
There is larger solid solubility in aluminum substrate, alloy is heated near solidus, held for some time, phase to be fortified is quenched after being completely dissolved
Fire obtains satiety solid solution, then carries out ageing treatment, make hardening constituent disperse educt again, plays solution strengthening and precipitating is strong
Change effect, so that alloy mechanical property be made to improve；In addition, heat treatment can significant nodularization eutectic Si, make its uniformly, Dispersed precipitate exists
In matrix, it can equally improve alloy mechanical property.
It since the fusing point of Si, Cu, Ni simple substance is higher, can be added in the form of intermediate alloy in fusion process, Al, Mg simple substance are molten
Point is low, can be added in fusion process with form of pure metal, and Sr is alterant, and dosage is few, therefore is added in the form of intermediate alloy.Separately
On the one hand, Al, Si are the component of eutectic Al-Si, therefore commercial-purity aluminium and Al-Si intermediate alloy can be used as base-material and first melted
Refining, Cu, Ni fusing point are higher, and to guarantee that it is sufficiently dissolved, Al-Cu intermediate alloy and Al-Ni intermediate alloy need to be after base-material fusings
Melting is put into again.The easy scaling loss of Mg, pure magnesium need to put into melting with aluminium foil package and finally.
Further embodiment is that the heat preservation time of repose in step B1 is 15min.
Further embodiment is that the dosage of step B1 coverture into B4 is the 0.5% to 0.7% of ingredient gross mass.
In view of coverture will take into account heat preservation and surface oxidation-resistant function to melt, its dosage is controlled in the total matter of ingredient
The 0.5% to 0.7% of amount is relatively inexpensive rationally.
Further embodiment is that the refining agent in step B3 is C2Cl6。
Further embodiment is that the dosage of refining agent is the 0.5% to 0.7% of ingredient gross mass in step B3.
C2Cl6It is more common refining agent, degasifying effect is preferable.The dosage of refining agent reaches above range in step B3
It can sufficiently play the role of taking into account economy while being vented deslagging.But since alterant Sr can be poisoned by Cl, Metamorphism treatment is needed
Using C2Cl6It is carried out after being refined.
Further embodiment is that the heat preservation time of repose in step B3 is 30min.
Heat preservation standing process, which reaches above-mentioned duration, so that melt is sufficiently refined, and thoroughly removes C2Cl6, prevent Sr first
Element is poisoned.
Further embodiment is that the heat preservation time of repose in step B4 is 25min to 35min.
Step D, which reaches above-mentioned heat preservation time of repose range, can be such that Sr element gives full play to multi-element eutectic Al-Si alloy
Metamorphism.
Further embodiment is that quenching shift time is not more than 25s in step D.
Above-mentioned quenching shift time refer to alloy cast ingot moved into from 510 DEG C of hot environment spent in hardening media when
Between, the temperature change that quenching shift time control can effectively avoid transfer process within the above range is influenced into consolidating for alloy cast ingot
Molten treatment effect.
The present invention is by targeted design of alloy, using reasonable melting and Sr Metamorphism treatment technique, in conjunction with
Heat treating regime appropriate can be obtained in high temperature (300 DEG C) and all have under room temperature the Al-Si-Cu- compared with high-tensile
Mg-Ni-Sr alloy.High temperature (300 DEG C) tensile strength of the alloy is not less than 125MPa, and room temperature tensile intensity is not less than
300MPa, the extraordinary piston that can be used for being produced on high temperature and there is higher service performance to require under room temperature, and due to heat
Solid solution and aging time are shorter in treatment process, comprehensive lower production costs.
Detailed description of the invention
Fig. 1 is the as cast condition metallograph for being not added with the eutectic Al-Si alloy ingot casting of Sr.
Fig. 2 is the as cast condition metallograph for adding the eutectic Al-Si alloy ingot casting of 0.02%Sr.
Fig. 3 is the as cast condition metallograph for adding the eutectic Al-Si alloy ingot casting of 0.04%Sr.
Fig. 4 is the as cast condition metallograph for adding the eutectic Al-Si alloy ingot casting of 0.06%Sr.
Fig. 5 is the as cast condition metallograph for adding the eutectic Al-Si alloy ingot casting of 0.08%Sr.
Fig. 6 is the DTA curve figure of Al-Si-Cu-Mg-Ni-Sr alloy cast ingot.
Fig. 7 is the metallograph for the Al-Si-Cu-Mg-Ni-Sr alloy material that embodiment 1 obtains.
Fig. 8 is the metallograph for the Al-Si-Cu-Mg-Ni-Sr alloy material that embodiment 2 obtains.
Fig. 9 is the metallograph for the Al-Si-Cu-Mg-Ni-Sr alloy material that embodiment 3 obtains.
The invention will be further described with reference to the accompanying drawings and embodiments.
Specific embodiment
The Sr element of different content is introduced under the premise of the mass fraction of Si is constant in keeping eutectic Al-Si alloy to altogether
The influence of the modification effect of brilliant Al-Si alloy structure is as shown in Fig. 1 to 5.From Fig. 1 to 5 it can be seen that without Sr Metamorphism treatment
Eutectic Al-Si alloy tissue in α-Al phase with Si phase be in typical coupled growth tissue；Rotten effect when Sr content is 0.02wt%
Fruit is not obvious, alloy structure with it is not rotten when it is almost the same；When the content of Sr increases to 0.04wt%, modification effect is aobvious
It writes, there are a large amount of tiny vermiform eutectic Si to occur in tissue, though still there is the long needle-shaped eutectic Si of certain amount, its length obviously becomes
It is short；When continuing growing Sr content to 0.06wt%, vermiform eutectic Si becomes more tiny, and the only needle-shaped eutectic Si of minute quantity
In the presence of, while α-Al occurs with granular form；When Sr content reaches 0.08wt%, eutectic Si is completely with tiny vermiform shape
Formula exists, and α-Al crystal grain is obviously grown up, but hole also occurs in tissue.It is best rotten to obtain eutectic Al-Si alloy
The content of effect, Sr should be 0.04%-0.06wt%.
It prepares and needs to the graphite clay crucible used before Al-Si-Cu-Mg-Ni-Sr alloy material, stirring rod, skims
The tool surfaces that spoon, mold etc. can contact melt are cleared up, and uniformly coating barrier coating on its surface later, (isolation applies
Material is deployed by the waterglass of ZnO, 10wt% and the water of 70wt% of 20wt%), and be dried for standby, baking temperature 250
DEG C to 300 DEG C.
Embodiment 1
A, ingredient: each element mass percent is Al:79.5%, Si in Al-Si-Cu-Mg-Ni-Sr alloy material:
13.0%, the ratio of Cu:4.5%, Mg:1.0%, Ni:2.0%, Sr:0.04% weigh commercial-purity aluminium (99.99%), Al-
20%Si intermediate alloy (quality of silicon account for intermediate alloy gross mass 20%), Al-50%Cu intermediate alloy are (during the quality of copper accounts for
Between alloy gross mass 50%), pure magnesium (99.99%), (it is total that the quality of nickel accounts for intermediate alloy to Al-10%Ni intermediate alloy
The 10% of quality) and Al-10%Sr intermediate alloy (quality of strontium account for intermediate alloy gross mass 10%) carry out ingredient.
B, 280 DEG C of graphite B1: melting: is pre-heated to using commercial-purity aluminium, Al-20%Si intermediate alloy as base-material addition
It in clay crucible, is then placed in and is heated to 770 DEG C in well formula smelting furnace and keeps constant temperature, stay the surface Shi Qi to base-material softening
Sprinkling dosage is 0.6% coverture of ingredient total weight (by CaO, 15wt% of 15wt% to 25wt% to 30wt%'s
Al2O3And the SiO of 40wt% to 50wt%2It is obtained after mixing).Heat preservation stands 15min after base-material is completely melt, is then added
Al-50%Cu intermediate alloy and Al-10%Ni intermediate alloy, are sufficiently stirred and skim after being completely melt.Forward sight of skimming melt table
The practical oxidization condition in face can also take the circumstances into consideration to add a small amount of coverture again, promote slag and melt separation and reduce the metal taken out of
Amount, process of skimming is steady, and slag is prevented to be involved in melt, while skimming and to be as far as possible thoroughly not thorough to avoid slag removing
Melt air content is caused to increase.
B2: the obtained melt of step B1 is cooled to 720 DEG C and is pressed into the pure magnesium wrapped up with aluminium foil with bell jar, then
Sprinkle 0.5% coverture that dosage is ingredient total weight in bath surface and stir to pure magnesium and be completely melt, then into
Row is skimmed.The concrete operation method skimmed is the same as step B1.
B3: the obtained solution of step B2 is warming up to 780 DEG C and sprinkles 0.7% covering that dosage is ingredient total weight
Agent is then pressed into 0.6% C that dosage is ingredient total weight with bell jar into melt2Cl6It is vented deslagging as refining agent, to nothing
Yellow gas is emerged, and subsequent continuation of insurance is warm to be stood 30min and skims, and the concrete operation method skimmed is the same as step B1.
B4: it is pressed into the Al-Sr intermediate alloy wrapped up with aluminium foil in the melt obtained with bell jar to step B3 and sprinkles dosage
For 0.65% coverture of ingredient total weight, heat preservation stands 30min and takes off after stirring is completely melt to Al-Sr intermediate alloy
Slag.The concrete operation method skimmed is the same as step B1.
C, it is poured: injecting melted melt into steel casting mould, obtain the alloy of 300 × 50 × 50mm after cooling
Ingot casting, casting process need to guarantee quick and stable.
Step C is obtained using inductively coupled plasma atomic emission spectrometer (LEEMANLabs, SPEC-E type)
Al-Si-Cu-Mg-Ni-Sr alloy cast ingot carries out composition detection, and testing result is shown in Table 1.The present embodiment uses as can be seen from Table 1
Smelting technology can prepare the alloy cast ingot that ingredient meets design requirement.
Table 1: the practical accounting of each element in the alloy cast ingot that embodiment 1 obtains
It is as shown in Figure 6 that the DTA curve figure that differential thermal analysis obtains is carried out to the alloy cast ingot that step C is obtained.It can from Fig. 6
There is endothermic thermal event at 538 DEG C in the alloy out, and eutectic reaction formula at this temperature is (α-Al)+(Si)+γ+Q+T → L, therefore
The solid solubility temperature of the alloy must not exceed 538 DEG C.Further it can determine that the alloy is suitble to using solution treatment+people by experiment
The mode of working hour effect (T6) is heat-treated, and optimal heat treating regime be 510 DEG C × 6h be dissolved+185 DEG C of (quenching) ×
6h timeliness.
D, solution treatment: the Al-Si-Cu- for being obtained step C using heat-treatment furnace (Hefei section is brilliant, KSL-1700X type)
Mg-Ni-Sr alloy cast ingot is heated to 510 DEG C, keeps the temperature 6h, then water quenching (be transferred in water and quenched) and is cooled to room temperature,
Quenching shift time is not more than 25s.
E, ageing treatment: the Al-Si-Cu-Mg-Ni-Sr alloy material that step D is obtained is warming up to using heat-treatment furnace
185 DEG C, 6h is kept the temperature, is then slowly cooled to room temperature to get Al-Si-Cu-Mg-Ni-Sr alloy material is arrived.
The metallograph of T6 state Al-Si-Cu-Mg-Ni-Sr alloy material made from this example is as shown in fig. 7, energy in Fig. 7
Enough see a large amount of tiny vermiform eutectic Si, illustrates that solid solution and ageing treatment combination Sr metamorphism change the pattern of eutectic Si
Kind effect is obvious.Stretching examination is carried out to the alloy material respectively in accordance with GB/T228.2-2015 and GB/T 228.1-2010 standard
It tests, measuring its tensile strength at 300 DEG C is 133MPa, and tensile strength at room temperature is 312MPa, can be used for being produced on height
The extraordinary piston for mildly thering is higher service performance to require under room temperature.
Embodiment 2
This implementation prepares T6 state Al-Si-Cu-Mg-Ni-Sr alloy material, area according to method substantially the same manner as Example 1
It is not only that:
According to Al:79.95wt%, Si:12.7wt%, Cu:4.4wt%, Mg:1.05wt%, Ni in step A:
The ratio of 1.9wt%, Sr:0.06wt% weigh commercial-purity aluminium, Al-20%Si intermediate alloy, Al-50%Cu intermediate alloy, work
The pure magnesium of industry, Al-10%Ni intermediate alloy and Al-10%Sr intermediate alloy carry out ingredient；
Step B1, the smelting temperature in B2, B3 is respectively 780 DEG C, 715 DEG C and 770 DEG C, and the dosage of coverture is respectively to match
Expect 0.5%, 0.6% and the 0.6% of gross weight；C in step B32Cl6Dosage be the 0.5% of ingredient total weight, keep the temperature in step B4
Time is 35min.
The Al-Si-Cu-Mg-Ni-Sr alloy that step C is obtained using inductively coupled plasma atomic emission spectrometer
Ingot casting carries out composition detection, and testing result is shown in Table 2.The smelting technology that the present embodiment uses as can be seen from Table 2 can be prepared
Ingredient meets the alloy cast ingot of design requirement.
Table 2: the practical accounting of each element in the alloy cast ingot that embodiment 2 obtains
The metallograph of T6 state Al-Si-Cu-Mg-Ni-Sr alloy material made from this example is as shown in figure 8, energy in Fig. 8
Enough see a large amount of tiny vermiform eutectic Si, illustrates that solid solution and ageing treatment combination Sr metamorphism change the pattern of eutectic Si
Kind effect is obvious.Stretching examination is carried out to the alloy material respectively in accordance with GB/T228.2-2015 and GB/T 228.1-2010 standard
It tests, measuring its tensile strength at 300 DEG C is 128MPa, and tensile strength at room temperature is 315MPa, can be used for making high temperature
The extraordinary piston for thering is higher service performance to require under room temperature.
Embodiment 3
This implementation prepares T6 state Al-Si-Cu-Mg-Ni-Sr alloy material, area according to method substantially the same manner as Example 1
It is not only that:
Step A according to Al:79.3wt%, Si:13.1wt%, Cu:4.6wt%, Mg:1.0wt%, Ni:2.0wt% and
The ratio of Sr:0.05wt% weigh commercial-purity aluminium, Al-20%Si intermediate alloy, Al-50%Cu intermediate alloy, pure magnesium,
Al-10%Ni intermediate alloy and Al-10%Sr intermediate alloy carry out ingredient；
Step B1, the smelting temperature in B2, B2 is respectively 790 DEG C, 725 DEG C and 790 DEG C, and the dosage of coverture is respectively to match
Expect 0.7%, 0.7% and the 0.5% of gross weight；C in step B32Cl6Dosage be the 0.7% of ingredient total weight, keep the temperature in step B4
Time is 25min.
The Al-Si-Cu-Mg-Ni-Sr alloy that step C is obtained using inductively coupled plasma atomic emission spectrometer
Ingot casting carries out composition detection, and testing result is shown in Table 3.The smelting technology that the present embodiment uses as can be seen from Table 3 can be prepared
Ingredient meets the alloy cast ingot of design requirement.
Table 3: the practical accounting of each element in the alloy cast ingot that embodiment 3 obtains
The metallograph of T6 state Al-Si-Cu-Mg-Ni-Sr alloy material made from this example is as shown in figure 9, energy in Fig. 9
Enough see a large amount of tiny vermiform eutectic Si, illustrates that solid solution and ageing treatment combination Sr metamorphism change the pattern of eutectic Si
Kind effect is obvious.Stretching examination is carried out to the alloy material respectively in accordance with GB/T228.2-2015 and GB/T 228.1-2010 standard
It tests, measuring its tensile strength at 300 DEG C is 128MPa, and tensile strength at room temperature is 305MPa, can be used for being produced on height
The extraordinary piston for mildly thering is higher service performance to require under room temperature.
Comparative example
According to Al:79.5wt%, Si:13.0wt%, Cu:4.5wt%, Mg:1.0wt%, Ni:2.0wt%, Sr:
The ratio of 0.06wt% weighs commercial-purity aluminium, Al-20%Si intermediate alloy, Al-50%Cu intermediate alloy, pure magnesium, Al-
10%Ni intermediate alloy and Al-10%Sr intermediate alloy carry out ingredient.And according to process described in step B in embodiment 1 and step C
Melting and casting are carried out, but without solution treatment and ageing treatment.
Using plasma Atomic Emission Spectrometer AES carries out into sorting obtained Al-Si-Cu-Mg-Ni-Sr alloy cast ingot
It surveys, testing result is shown in Table 4.The alloy material is carried out respectively in accordance with GB/T 228.2-2015 and GB/T228.1-2010 standard
Tension test, measuring its tensile strength at 300 DEG C is 140MPa, and tensile strength at room temperature is 247MPa, by comparing
Reasonable solid solution and ageing treatment known to tensile strength values of the alloy material that embodiment and comparative example obtains under corresponding temperature
It can guarantee that Al-Si-Cu-Mg-Ni-Sr alloy material is also equipped with while having certain high temperature (300 DEG C) tensile property
Preferable room temperature tensile performance.
Table 4: the practical accounting of each element in the alloy cast ingot that comparative example obtains
Claims (10)
1. a kind of Al-Si-Cu-Mg-Ni-Sr alloy material, which is characterized in that by mass percentage containing 12.35% to
13.65% Si, 4.28% to 4.73% Cu, 0.95% to 1.05% Mg, 1.90% to 2.10% Ni, 0.04% to
0.06% Sr, surplus are aluminium and inevitable impurity, total impurities≤0.1%.
2. a kind of piston, which is characterized in that the piston is by Al-Si-Cu-Mg-Ni-Sr alloy material described in claim 1
It is made.
3. a kind of preparation method of Al-Si-Cu-Mg-Ni-Sr alloy material, which comprises the following steps:
A, ingredient: according to each element mass percent in Al-Si-Cu-Mg-Ni-Sr alloy material be Si:12.35% extremely
13.65%, Cu:4.28% to 4.73%, Mg:0.95% to 1.05%, Ni:1.90% to 2.10%, Sr:0.04% extremely
0.06% and balance aluminum ratio, weigh Al-Si intermediate alloy, Al-Cu intermediate alloy, pure magnesium, Al-Ni intermediate alloy,
Al-Sr intermediate alloy and commercial-purity aluminium；
B, melting: B1, using the weighed commercial-purity aluminium of step A and Al-Si intermediate alloy as being heated in base-material investment smelting furnace
770 DEG C to 790 DEG C and constant temperature is kept, coverture is sprinkled when base-material softening stays, base-material keeps the temperature after being completely melt and stands, then
Al-Cu intermediate alloy and Al-Ni intermediate alloy is added, is sufficiently stirred and skims after being completely melt；B2, it is melted what step B1 was obtained
Body is cooled to 715 DEG C to 725 DEG C and the pure magnesium wrapped up with aluminium foil is added, then sprinkle coverture and stirs to pure magnesium
It is completely melt, then skims；B3, the obtained solution of step B2 is warming up to 770 DEG C to 790 DEG C and sprinkles coverture, with
Refining agent is added in backward melt and is vented deslagging, heat preservation is skimmed after standing；It is added in B4, the melt obtained to step B3 with aluminium foil
The Al-Sr intermediate alloy of package simultaneously sprinkles coverture, and heat preservation stands and skims after stirring is completely melt to Al-Sr intermediate alloy；
C, cast: the melt that injection step B is obtained into casting mould obtains alloy cast ingot after cooling；
D, solution treatment: the obtained alloy cast ingot of step C is heated to 510 DEG C, quenches and is cooled to room temperature after keeping the temperature 6h；
E, ageing treatment: the obtained alloy cast ingot of step D is heated to 185 DEG C, is slowly cooled to room temperature, obtains after keeping the temperature 6h
Al-Si-Cu-Mg-Ni-Sr alloy material.
4. the preparation method of Al-Si-Cu-Mg-Ni-Sr alloy material as claimed in claim 3, which is characterized in that step B1
In heat preservation time of repose be 15min.
5. the preparation method of Al-Si-Cu-Mg-Ni-Sr alloy material as claimed in claim 3, which is characterized in that step B1
Into B4, the dosage of coverture is the 0.5% to 0.7% of ingredient gross mass.
6. the preparation method of Al-Si-Cu-Mg-Ni-Sr alloy material as claimed in claim 3, which is characterized in that step B3
In refining agent be C2Cl6。
7. the preparation method of Al-Si-Cu-Mg-Ni-Sr alloy material as claimed in claim 3, which is characterized in that step B3
The dosage of middle refining agent is the 0.5% to 0.7% of ingredient gross mass.
8. the preparation method of Al-Si-Cu-Mg-Ni-Sr alloy material as claimed in claim 3, which is characterized in that step B3
In heat preservation time of repose be 30min.
9. the preparation method of Al-Si-Cu-Mg-Ni-Sr alloy material as claimed in claim 3, which is characterized in that step B4
In heat preservation time of repose be 25min to 35min.
10. the preparation method of Al-Si-Cu-Mg-Ni-Sr alloy material as claimed in claim 3, which is characterized in that step D
Middle quenching shift time is not more than 25s.
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